Chemically strengthened glass and method for producing same

ABSTRACT

A chemically strengthened glass having a compressive stress layer formed in a surface layer thereof according to an ion exchange method, in which a surface of the glass has polishing flaws, the glass has a texture direction index (Stdi) of 0.30 or more, a hydrogen concentration Y in a region to a depth X from an outermost surface of the glass satisfies the following relational equation (I) at X=from 0.1 to 0.4 (μm), and a surface strength F (N) measured by a ball-on-ring test is (F≥1400×t 2 ) relative to a sheet thickness t (mm) of the glass:
 
 Y=aX+b   (I)
 
in which meanings of respective symbols in the equation (I) are as follows: Y: hydrogen concentration (as H 2 O, mol/L), X: depth from the outermost surface of the glass (μm), a: −0.300 or more, and b: 0.220 or less.

TECHNICAL FIELD

The present invention relates to a chemically strengthened glass and a method for producing the same.

BACKGROUND ART

In flat panel display devices such as digital cameras, mobile phones, personal digital assistants (PDAs), etc., in order to protect displays and enhance the appearance thereof, a thin plate-like cover glass is disposed on the front surface of the display so as to provide a broader region than an image display portion. Although the glass has a high theoretical strength, when scratched, its strength is largely lowered, and therefore, for the cover glass that is required to satisfy strength, a chemically strengthened glass having a compressive stress layer formed on the surface thereof through ion exchange or the like is used.

With the growing demand for weight reduction and thickness reduction in flat panel display devices, it is desired to thin cover glass itself. Accordingly, for satisfying the purpose, both the surfaces and the edge surfaces of cover glass are desired to have further strength.

For increasing the strength of the chemically strengthened glass, heretofore, a surface etching treatment to be conducted after chemical strengthening treatment is known (Patent Document 1).

Here, regarding the strength of glass, it is known that the strength of glass is lowered by the existence of hydrogen (water) in glass (Non-Patent Documents 1 and 2).

BACKGROUND ART DOCUMENT Patent Document

-   Patent Document 1: JP-T-2013-516387

Non-Patent Document

-   Non-Patent Document 1: S. ITO et. al., “Crack Blunting of     High-Silica Glass”, Journal of the American Ceramic Society, Vol.     65, No. 8, (1982), 368-371 -   Non-Patent Document 2: Won-Taek Han et. al., “Effect of residual     water in silica glass on static fatigue”, Journal of Non-Crystalline     Solids, 127, (1991) 97-104

SUMMARY OF THE INVENTION Problems that the Invention is to Solve

The present inventors have found that there is a concern that the strength of glass is lowered after the chemical strengthening, and the major cause thereof is that moisture in the atmosphere penetrates into the glass surface layer to form chemical defects. Further, the present inventors have found that this phenomenon occurs not only through chemical strengthening but also through a heating step in glass production process.

As a technique for removing moisture from a glass surface layer, it may be considered to chip off the moisture-containing layer according to a technique of polishing the glass surface after chemical strengthening or according to a technique of subjecting the glass surface after chemical strengthening to an etching treatment by immersing in hydrofluoric acid or the like. However, there is a concern that the surface of glass is scratched by polishing so that the strength thereof rather lowers. In addition, in a case where the glass surface has latent flaws, there is a concern that the etching treatment using hydrofluoric acid or the like grows the latent flaws to cause appearance failure owing to pits. Further, hydrofluoric acid requires careful handling in view of safety.

An object of the present invention is to provide a chemically strengthened glass capable of effectively preventing the strength of glass from lowering even after performing chemical strengthening.

Means for Solving the Problems

The present inventors have found that by not only allowing a hydrogen concentration profile on a surface layer of a chemically strengthened glass to fall within a specific range but also controlling a texture direction index (Stdi) of a glass surface to a specific value or more, even when the glass surface is polished, the surface strength of the glass is tremendously improved, thereby accomplishing the present invention.

Namely, the present invention is as shown below.

[1] A chemically strengthened glass having a compressive stress layer formed in a surface layer thereof according to an ion exchange method,

in which a surface of the glass has polishing flaws,

the glass has a texture direction index (Stdi) of 0.30 or more,

a hydrogen concentration Y in a region to a depth X from an outermost surface of the glass satisfies the following relational equation (I) at X=from 0.1 to 0.4 (μm), and

a surface strength F (N) measured by a ball-on-ring test under the following conditions is (F≥1400×t²) relative to a sheet thickness t (mm) of the glass: Y=aX+b  (I) in which meanings of respective symbols in the equation (1) are as follows:

Y: hydrogen concentration (as H₂O, mol/L);

X: depth from the outermost surface of the glass (μm);

a: −0.300 or more; and

b: 0.220 or less,

the conditions of the ball-on-ring test:

a sheet of the glass having the sheet thickness t (mm) is disposed on a stainless ring whose diameter is 30 mm and whose contact part has a roundness with a curvature radius of 2.5 mm; while a steel ball having a diameter of 10 mm is kept in contact with the sheet of the glass, a center of the ring is subjected to a load by the ball under a static loading condition; and a fracture load (unit: N) at which the glass is fractured is taken as a BOR surface strength and an average value of twenty measured values thereof is taken as the surface strength F, provided that in a case where a fracture origin of the glass is separated from a loading point of the ball by 2 mm or more, the obtained value is excluded from data for calculating the average value.

[2] The chemically strengthened glass according to [1], in which the glass is an aluminosilicate glass, an aluminoborosilicate glass or a soda-lime glass.

[3] The chemically strengthened glass according to [1] or [2], having a texture aspect ratio (Str20) of 0.10 or more.

[4] A method for producing a chemically strengthened glass, including a step of bringing a glass containing sodium into contact with an inorganic salt containing potassium nitrate, thereby performing ion exchange of a Na ion in the glass with a K ion in the inorganic salt,

in which the inorganic salt contains at least one salt selected from the group consisting of K₂CO₃, Na₂CO₃, KHCO₃, NaHCO₃, K₃PO₄, Na₃PO₄, K₂SO₄, Na₂SO₄, KOH and NaOH, and

the method includes:

a step of polishing a surface of the glass before the ion exchange;

a step of washing the glass after the ion exchange;

a step of subjecting the glass to an acid treatment after the washing; and

a step of subjecting the glass to an alkali treatment after the acid treatment.

[5] A chemically strengthened glass obtained by the production method according to [4].

Advantage of the Invention

According to the chemically strengthened glass of the present invention, by allowing the hydrogen concentration profile on the glass surface layer to fall within a specific range and controlling the texture direction index (Stdi) of the glass surface to a specific value or more, it is possible to significantly improve the surface strength of the glass.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic view for explaining a method of a ball-on-ring test.

FIG. 2 A schematic view showing a production process of a chemically strengthened glass according to the present invention is shown in (a) to (d) of FIG. 2.

FIG. 3 is a graph of plotting the hydrogen concentration profile in the surface layer of each chemically strengthened glass obtained in Examples 1 to 2 and Comparative Examples 1 to 2.

FIG. 4 is an explanatory view for deriving the relational equation (I) from the graph of plotting the hydrogen concentration profile in the surface layer of the chemically strengthened glass obtained in Example 1.

FIG. 5 is an explanatory view for deriving the relational equation (I) from the graph of plotting the hydrogen concentration profile in the surface layer of the chemically strengthened glass obtained in Comparative Example 1.

FIG. 6 is an AFM image of a glass surface of Example 1.

FIG. 7 is an AFM image of a glass surface of Example 2.

FIG. 8 is an AFM image of a glass surface of Example 3.

FIG. 9 is an AFM image of a glass surface of Comparative Example 1.

FIG. 10 is an AFM image of a glass surface of Comparative Example 2.

FIG. 11 is an AFM image of a glass surface of Comparative Example 3.

FIG. 12 is an AFM image of a glass surface of Reference Example 1.

FIG. 13 is an AFM image of a glass surface of Reference Example 2.

FIG. 14 is a Weibull plot of BOR surface strength evaluation of each of chemically strengthened glasses obtained in Example 1 and Comparative Example 1.

MODE FOR CARRYING OUT THE INVENTION

The present invention is hereunder described in detail, but it should not be construed that the present invention is limited to the following embodiments, and the present invention may be arbitrarily modified and carried out within the range where the gist of the present invention is not deviated.

<Chemically Strengthened Glass>

The chemically strengthened glass according to the present invention is a chemically strengthened glass having a compressive stress layer formed in the surface layer thereof according to an ion exchange method, in which the hydrogen concentration in the region to a certain depth from the outermost surface of the glass satisfies the following relational equation (I), and the glass surface has polishing flaws.

The compressive stress layer is a high-density layer formed through ion exchange of the Na ion in a glass surface with the K ion in a molten salt by bringing a starting material glass into contact with an inorganic molten salt such as potassium nitrate.

In the chemically strengthened glass of the present invention, the hydrogen concentration profile in the glass surface layer falls within a specific range. Specifically, the hydrogen concentration Y in a region to a depth X from the outermost surface of the glass satisfies the following relational equation (I) at X=from 0.1 to 0.4 (μm). Y=aX+b  (I) [In the equation (I), the meanings of the respective symbols are as follows:

Y: hydrogen concentration (as H₂O, mol/L)

X: depth from the outermost surface of glass (μm)

a: −0.300 or more

b: 0.220 or less]

Regarding the surface strength of a glass, it is known that the surface strength of a glass lowers owing to the presence of hydrogen (moisture) in the glass, but the present inventors have found that there is a concern that the surface strength of glass is lowered after the chemical strengthening treatment, and the major cause thereof is that moisture in the atmosphere penetrates into the glass to form chemical defects. Further, the present inventors have found that this phenomenon occurs not only through the chemical strengthening but also through a heating step in glass production process.

When the hydrogen concentration in a glass is high, hydrogen penetrates into the Si—O—Si bond network in the glass in the form of Si—OH whereby the bond of Si—O—Si is cut. When the hydrogen concentration in the glass is high, it is considered that the part where the Si—O—Si bond is cut increases so that chemical defects may be easily formed, whereby the surface strength is lowered.

The above-mentioned relational equation (I) holds in a region of from the outermost surface to a depth X=from 0.1 to 0.4 The thickness of the compressive stress layer to be formed through ion exchange falls within a range of from 5 to 50 μm, though it depends on the degree of chemical strengthening. The hydrogen penetration depth into glass follows the diffusion coefficient, temperature and time, and the hydrogen penetration amount is influenced by the moisture amount in the atmosphere in addition to these. The hydrogen concentration after chemical strengthening is the highest in the outermost layer and gradually reduces toward the deep part (bulk) where the compressive stress layer is not formed. The above-mentioned relational equation (I) defines the profile of the reduction, and in the outermost surface (X=0 μm), there is a possibility that the moisture concentration may vary owing to time-dependent degradation, and therefore the equation is defined to hold in a region of the near surface (X=from 0.1 to 0.4 μm) not influenced by the variation.

In the equation (I), a indicates an inclination to define the profile of reduction in the hydrogen concentration. The range of a is −0.300 or more, preferably from −0.270 to −0.005, more preferably from −0.240 to −0.030.

In the equation (I), b corresponds to the hydrogen concentration in the outermost surface (X=0 μm). The range of b is 0.220 or less, preferably from 0.020 to 0.215, more preferably from 0.030 to 0.210.

In general, the surface strength reduction of a glass is considered to be caused by growth of microcracks existing in the glass surface owing to the mechanical stress given thereto from the outside. According to Non-Patent Document 2, when the glass structure at the tip of a crack is in a Si—OH-richer state, it is considered that the cracks easily grow. Assuming that the tips of cracks are exposed out in the atmosphere, the Si—OH amount in the tip of the crack is presumed to have a positive relationship to the hydrogen concentration in the glass outermost surface. Accordingly, b corresponding to the hydrogen concentration in the outermost surface preferably falls within a low range to the degree as shown above.

As shown in FIG. 3, the glass processed through a chemical strengthening step did not show any remarkable difference in the hydrogen penetration depth. There is a possibility that the hydrogen penetration depth may vary depending on the condition of the chemical strengthening step, but if the depth does not change at all, there appears a negative correlation between b that corresponds to the hydrogen concentration in the outermost surface and a that corresponds to the inclination to define the profile of reduction in the hydrogen concentration. Accordingly, a preferably falls within a high range to a degree as shown above.

As described above, in the present invention, it has been found that, not only by defining the hydrogen concentration itself alone in the surface layer but also by defining the hydrogen concentration in the surface layer and the reduction profile thereof each to fall within a specific range, with taking particular note of the hydrogen concentration profile, the surface strength of chemically strengthened glass can be greatly improved.

[Method for Measuring Hydrogen Concentration Profile]

Here, the hydrogen concentration profile (H₂O concentration, mol/L) of a glass is a profile measured under the following analysis condition.

For measurement of the hydrogen concentration profile of a glass substrate, a method of secondary ion mass spectrometry (SIMS) is employed. In a case where a quantitative hydrogen concentration profile is obtained through SIMS, a standard sample whose hydrogen concentration is known is necessary. A method for preparing the standard sample and a method for determination of the hydrogen concentration thereof are described below.

1) A part of the glass substrate to be analyzed is cut out.

2) A region of 50 μm or more from the surface of the thus-cut glass substrate is removed by polishing or chemical etching. The removal treatment is carried out on both surfaces. Namely, the thickness to be removed on both surfaces is 100 μm or more. The glass substrate that has been subjected to the removal treatment is used as a standard sample. 3) The standard sample is analyzed through infrared spectroscopy (IR), and the absorbance height A₃₅₅₀ at the peak top near 3,550 cm⁻¹ in the IR spectrum and the absorbance height A₄₀₀₀ (base line) at 4,000 cm⁻¹ are determined. 4) The thickness d (cm) of the standard sample is measured using a thickness measuring device such as a micrometer. 5) With reference to the reference A, the hydrogen concentration (as H₂O, mol/L) in the standard sample is determined using the formula II, in which the infrared practical absorbance index of H₂O in glass ε_(pract) (L/(mol·cm)) is 75. Hydrogen concentration in standard sample=(A ₃₅₅₀ −A ₄₀₀₀)/(ε_(pract) ·d)   Formula II

Reference A): S. Ilievski et al., Glastech. Ber. Glass Sci. Technol., 73 (2000) 39.

The glass substrate to be analyzed and the standard sample whose hydrogen concentration is known, as prepared according to the above-mentioned method, are simultaneously fed into a SIMS device, and analyzed sequentially to obtain the depth direction profiles of the intensities of ¹H⁻ and ³⁰Si⁻. Subsequently, the ¹H⁻ profile is divided by the ³⁰Si⁻ profile to obtain a depth direction profile of ¹H⁻/³⁰Si⁻ intensity ratio. From the depth direction profile of the ¹H⁻/³⁰Si⁻ intensity ratio of the standard sample, an average ¹H⁻/³⁰Si⁻ intensity ratio in a region of a depth of from 1 μm to 2 μm is calculated, and a calibration curve of this value and the hydrogen concentration is drawn to pass through the origin (calibration curve with one-level standard sample). Using the calibration curve, the ¹H⁻/³⁰Si⁻ intensity ratio on the vertical axis of the profile of the glass substrate to be analyzed is converted into the hydrogen concentration. Accordingly, the hydrogen concentration profile of the glass substrate to be analyzed is obtained. The measurement conditions in SIMS and IR are as follows.

[SIMS Measurement Condition]

Device: ADEPT1010 manufactured by ULVAC-PHI, Inc.,

Primary ion species: Cs⁺

Primary ion accelerating voltage: 5 kV

Primary ion current value: 500 nA

Primary ion incident angle: 60° relative to the normal line of the sample plane

Primary ion luster size: 300×300 μm²

Secondary ion polarity: minus

Secondary ion detection region: 60×60 μm² (4% of luster size of primary ion)

ESA Input Lens: 0

Use of neutralization gun: yes

Method of converting the horizontal axis from sputtering time to depth: The depth of the analysis crater is measured with a stylus surface profile analyzer (Dektak 150, manufactured by Veeco Inc.), and the primary ion sputtering rate is determined. Using the sputtering rate, the horizontal axis is converted from the sputtering time to the depth. Field Axis Potential in ¹H⁻ detection: The optimum value may change in every device. The operator should carefully define the value so that the background is fully cut off. [IR Measurement Condition] Device: Nic-plan/Nicolet 6700, manufactured by Thermo Fisher Scientific Co., Ltd. Resolution: 4 cm⁻¹ Number of scans: 16 Detector: TGS detector

For deriving the relational equation (I) from the hydrogen concentration profile (H₂O concentration, mol/L) of the glass determined under the above-mentioned analysis condition, the following procedure is employed. As shown in FIG. 4 and FIG. 5, linear approximation is applied to the hydrogen concentration profile in a region of a depth of from 0.1 to 0.4 μm. The equation of the resultant approximation straight line is referred to as the relational equation (I).

As a means of controlling a and b, for example, the fusing agent concentration, sodium concentration, temperature and time in the chemical strengthening step may be changed.

The chemically strengthened glass of the present invention has polishing flaws on the surface thereof. Here, polishing in the present invention means that the surface of a glass is polished with abrasives for smoothing. A method of surface polishing is not particularly limited, and examples thereof include usual methods. The presence or absence of polishing flaws may be discerned through surface observation with AFM (Atomic Force Microscope). A case where one or more scratches having a length of 5 μm or more are present in a region of 10 μm×5 μm can be said to be in a state that the surface has polishing flaws. FIG. 6 shows a state having surface polishing flaws (in Example 1 to be given below), and FIG. 12 shows a state not having surface polishing flaws (in Reference Example 1 to be given below).

(Glass Surface Strength)

The surface strength of the chemically strengthened glass of the present invention can be evaluated according to a ball-on-ring test.

(Ball-on-Ring Test)

The chemically strengthened glass of the present invention is evaluated in terms of the BOR surface strength F (N) measured by a ball-on-ring (BOR) test, in which a glass sheet is disposed on a stainless ring whose diameter is 30 mm and whose contact part has a roundness with a curvature radius of 2.5 mm, and while a steel ball having a diameter of 10 mm is kept in contact with the glass sheet, the center of the ring is subjected to a load by the ball under a static loading condition.

The chemically strengthened glass of the present invention satisfies F≥1,400×t², preferably F≥1,800×t². [In the formulae, F means the BOR surface strength (N) measured by the ball-on-ring test, and t means the thickness (mm) of the glass sheet.] When the BOR surface strength F (N) falls within the range, the glass exhibits an excellent surface strength even when formed into a thin sheet.

FIG. 1 shows a schematic view for explaining the ball-on-ring test used in the present invention. In the ball-on-ring (BOR) test, a glass sheet 1 is, while kept set horizontally, pressurized by a pressurizing jig 2 made of SUS304 (hardened steel, diameter: 10 mm, mirror-finished) to measure the surface strength of the glass sheet 1.

In FIG. 1, the glass sheet 1 to be a sample is horizontally set on a receiving jig 3 made of SUS304 (diameter: 30 mm, radius of curvature of the contact part R: 2.5 mm, the contact part is hardened steel, mirror-finished). Above the glass sheet 1, a pressurizing jig 2 for pressurizing the glass sheet 1 is arranged.

In this embodiment, the center region of the glass sheet 1 obtained in Examples and Comparative Examples is pressurized from above. The test condition is as mentioned below.

Descending Rate of Pressurizing Jig 2: 1.0 (mm/min)

In this test, the fracture load (unit: N) at which the glass is fractured is taken as a BOR surface strength. The average value of twenty measured values thereof is taken as a surface strength F. However, in a case where the fracture origin of the glass sheet is separated from a loading point of the ball by 2 mm or more, the obtained value is excluded from the data for calculating the average value.

(Texture Direction Index (Stdi))

Furthermore, in the chemically strengthened glass of the present invention, a texture direction index (Stdi) thereof is 0.30 or more, preferably 0.45 or more, and more preferably 0.50 or more. The texture direction index (Stdi) as referred to herein is an index exhibiting superiority or inferiority of directionality of the texture formed on the surface and takes a value of from 0 to 1. In the case where the texture has a superior direction, the Stdi becomes close to 0. On the other hand, in the case where the texture does not have directionality, the Stdi becomes close to 1. That is, in the case where the texture has a superior direction as in polishing flaws, the Stdi takes a value close to 0. However, when the polishing flaws become smooth, and the texture becomes indistinct, it may be considered that the Stdi becomes close to 1. It may be considered that in view of the fact that the texture direction index (Stdi) of the chemically strengthened glass of the present invention falls within the foregoing range, the chemically strengthened glass of the present invention has smooth polishing flaws.

After obtaining a shape image by an atomic force microscope (AFM), the texture direction index (Stdi) may be determined by an image analysis software.

(Texture Aspect Ratio (Str20))

The chemically strengthened glass of the present invention also preferably has a texture aspect ratio (Str20) of 0.10 or more, more preferably 0.35 or more, and still more preferably 0.55 or more. It may be considered that when the texture aspect ratio (Str20) falls within the foregoing range, the chemically strengthened glass of the present invention has smooth polishing flaws.

After obtaining a shape image by an atomic force microscope (AFM), the texture aspect ratio (Str20) may be determined by an image analysis software.

In addition, the chemically strengthened glass of the present invention is less in light scattering to be caused due to a pit and is excellent in surface appearance.

<Method for Producing Chemically Strengthened Glass>

One embodiment of the method for producing a chemically strengthened glass of the present invention is described below, to which, however, the present invention is not limited.

(Glass Composition)

Glass for use in the present invention may be any one containing sodium, and so far as it has a composition capable of being shaped and strengthened through chemical strengthening treatment, various types of compositions can be used. Specifically, for example, there are mentioned an aluminosilicate glass, a soda-lime glass, a boron silicate glass, a lead glass, an alkali barium glass, an aluminoborosilicate glass, etc.

The production method for a glass is not specifically limited. Desired glass raw materials are put into a continuous melting furnace, and the glass raw materials are melted under heat at preferably from 1,500 to 1,600° C., then refined and fed into a shaping device to shape the molten glass into a plate-like shape and gradually cooled to produce a glass.

Various methods may be employed for shaping a glass. For example, various shaping processes such as a down-draw process (for example, an overflow down-draw process, a slot-down process, a redraw process, etc.), a float process, a roll-out process, and a pressing process may be employed.

The thickness of a glass is not specifically limited, but for effectively conducting chemical strengthening treatment, in general, the thickness thereof is preferably 5 mm or less, more preferably 3 mm or less.

The shape of a glass for use in the present invention is not specifically limited. For example, various shapes of a glass such as a plate-like shape having a uniform thickness, a curved shape in which at least one of the front surface or the back surface is curved, and a three-dimensional shape having a bend portion are employable.

Although the composition of the chemically strengthened glass of the present invention is not specifically limited, for example, the following glass compositions may be mentioned.

(i) Glass having a composition including, in terms of mol %, from 50 to 80% of SiO₂, from 2 to 25% of Al₂O₃, from 0 to 10% of Li₂O, from 0 to 18% of Na₂O, from 0 to 10% of K₂O, from 0 to 15% of MgO, from 0 to 5% of CaO and from 0 to 5% of ZrO₂.

(ii) Glass having a composition including, in terms of mol %, from 50 to 74% of SiO₂, from 1 to 10% of Al₂O₃, from 6 to 14% of Na₂O, from 3 to 11% of K₂O, from 2 to 15% of MgO, from 0 to 6% of CaO and from 0 to 5% of ZrO₂, in which the total content of SiO₂ and Al₂O₃ is 75% or less, the total content of Na₂O and K₂O is from 12 to 25%, and the total content of MgO and CaO is from 7 to 15%.

(iii) Glass having a composition including, in terms of mol %, from 68 to 80% of SiO₂, from 4 to 10% of Al₂O₃, from 5 to 15% of Na₂O, from 0 to 1% of K₂O, from 4 to 15% of MgO and from 0 to 1% of ZrO₂.

(iv) Glass having a composition including, in terms of mol %, from 67 to 75% of SiO₂, from 0 to 4% of Al₂O₃, from 7 to 15% of Na₂O, from 1 to 9% of K₂O, from 6 to 14% of MgO and from 0 to 1.5% of ZrO₂, in which the total content of SiO₂ and Al₂O₃ is from 71 to 75%, the total content of Na₂O and K₂O is from 12 to 20%, and the content of CaO, if any, is less than 1%.

The chemically strengthened glass of the present invention has an ion-exchanged compressive stress layer in the surface thereof. In the ion exchange method, the surface of a glass is ion-exchanged to form a surface layer in which compressive stress remains. Specifically, the alkali metal ion (typically Li ion, Na ion) having a small ionic radius in the surface of a glass sheet is substituted with an alkali ion having a larger ionic radius (typically Na ion or K ion for Li ion, and K ion for Na ion) through ion exchange at a temperature not higher than the glass transition point. Accordingly, compressive stress remains in the surface of the glass, and the surface strength of the glass is thereby increased.

In the production method of the present invention, chemical strengthening is conducted by bringing a glass into contact with an inorganic salt containing potassium nitrate (KNO₃). Accordingly, the Na ion in the glass surface is ion-exchanged with the K ion in the inorganic salt to form a high-density compressive stress layer. The method for bringing a glass into contact with an inorganic salt includes a method of applying a pasty inorganic salt to a glass, a method of spraying a glass with an aqueous solution of an inorganic salt, and a method of immersing a glass in a salt bath of a molten salt heated at a temperature not lower than the melting point thereof, and of these, a method of immersing in a molten salt is desirable.

The inorganic salt is preferably one having a melting point not higher than the strain point of the glass to be strengthened (generally 500 to 600° C.), and in the present invention, a salt containing potassium nitrate (melting point: 330° C.) is used. Containing potassium nitrate, the salt is capable of being in a molten state at a temperature not higher than the strain point of the glass and, in addition, capable of being easily handled in the operating temperature range. The content of the potassium nitrate in the inorganic salt is preferably 50% by mass or more.

Additionally, the inorganic salt contains at least one salt selected from the group consisting of K₂CO₃, Na₂CO₃, KHCO₃, NaHCO₃, K₃PO₄, Na₃PO₄, K₂SO₄, Na₂SO₄, KOH and NaOH, and above all, preferably contains at least one salt selected from the group consisting of K₂CO₃, Na₂CO₃, KHCO₃ and NaHCO₃.

The above-mentioned salt (hereinafter this may be referred to as “fusing agent”) has a property of cutting the network of a glass typified by an Si—O—Si bond. Since the temperature at which chemical strengthening treatment is conducted is high such as a few hundred degrees C., the covalent bond between Si—O in a glass is suitably cut at that temperature and therefore the density-reducing treatment to be mentioned below for the glass can be easy to promote.

The degree of cutting the covalent bond may vary depending on the glass composition, the type of the salt (fusing agent) to be used, and the chemical strengthening treatment conditions such as the temperature and the time, but is considered to be preferably selected from the conditions under which from 1 to 2 bonds of the four covalent bonds extending from Si can be cut.

For example, in a case where K₂CO₃ is used as a fusing agent, the content of the fusing agent in the inorganic salt is 0.1 mol % or more and the chemical strengthening treatment temperature is from 350 to 500° C., the chemical strengthening treatment time is preferably from 1 minute to 10 hours, more preferably from 5 minutes to 8 hours, even more preferably from 10 minutes to 4 hours.

The amount of the fusing agent to be added is, from the viewpoint of surface hydrogen concentration control, preferably 0.1 mol % or more, more preferably 1 mol % or more, and particularly preferably 2 mol % or more. From the viewpoint of productivity, the amount thereof is preferably not larger than the saturation solubility of each salt. When the fusing agent is excessively added, there is a concern of causing glass corrosion. For example, in a case where K₂CO₃ is used as the fusing agent, the amount thereof is preferably 24 mol % or less, more preferably 12 mol % or less, particularly preferably 8 mol % or less.

The inorganic salt may contain any other chemical species within a range not impairing the advantageous effects of the present invention, in addition to potassium nitrate and the fusing agent. For example, there are mentioned alkali chloride salts or alkali borate salts such as sodium chloride, potassium chloride, sodium borate, and potassium borate. One or more of these may be added either singly or as combined.

(Step 1: Polishing of Glass Surface)

In the step 1, the glass surface is polished. The polishing conditions are not particularly limited, and the polishing may be performed under conditions so as to obtain a desired surface roughness. As for polishing means, the polishing may be performed by a general method in which, for example, cerium oxide having an average particle diameter of about 0.7 μm is dispersed in water to prepare a slurry having a specific gravity of 0.9, and the glass surface is polished in a depth of 0.5 μm or more per surface with a polishing pad of a nonwoven type or suede type under conditions of a polishing pressure of 10 kPa.

By polishing the glass surface, macro flaws on the glass surface are removed, whereby the surface strength can be improved. The polishing of the glass surface is performed before a chemical strengthening treatment (ion exchange) of a step 4 as described later.

The production method of the present invention is hereunder described with reference to examples of an embodiment in which chemical strengthening is performed according to a method of immersing a glass in a molten salt.

(Production of Molten Salt 1)

A molten salt may be produced according to steps mentioned below.

Step 2a: Preparation of potassium nitrate molten salt

Step 3a: Addition of fusing agent to the potassium nitrate molten salt

(Step 2a—Preparation of Potassium Nitrate Molten Salt—)

In the step 2a, potassium nitrate is put into a container, and melted by heating at a temperature not lower than the melting point thereof to prepare a molten salt. The melting is conducted at a temperature falling within a range of from the melting point (330° C.) of potassium nitrate to the boiling point (500° C.) thereof. In particular, it is more preferable that the melting temperature is from 350 to 470° C. from the viewpoint of the balance between the surface compressive stress (CS) to be given to a glass and the depth of the compressive stress layer (DOL) and of the strengthening time.

Regarding the container for melting potassium nitrate, metals, quartz, ceramics and the like can be used. Above all, from the viewpoint of durability, metal materials are desirable, and from the viewpoint of corrosion resistance, stainless steel (SUS) materials are preferred.

(Step 3a—Addition of Fusing Agent to the Potassium Nitrate Molten Salt—)

In the step 3a, the above-mentioned fusing agent is added to the potassium nitrate molten salt prepared in the step 2a, and, while kept at a temperature falling within a certain definite range, mixed with an impeller or the like so that the whole becomes uniform. In a case where plural fusing agents are used, the order of adding them is not specifically limited, and these may be added at a time.

The temperature is preferably not lower than the melting point of potassium nitrate, that is, preferably 330° C. or higher, more preferably from 350 to 500° C. The stirring time is preferably from 1 minute to 10 hours, more preferably from 10 minutes to 2 hours.

(Production of Molten Salt 2)

In the above-mentioned production of molten salt 1, a method of adding a fusing agent after preparation of a molten salt of potassium nitrate is exemplified, but apart from the method, the molten salt may also be produced according to the following steps.

Step 2b: mixing of potassium nitrate and fusing agent

Step 3b: melting of mixed salt of potassium nitrate and fusing agent

(Step 2b—Mixing of Potassium Nitrate and Fusing Agent—)

In the step 2b, potassium nitrate and a fusing agent are put into a container and mixed with an impeller or the like. In a case where plural fusing agents are used, the order of adding them is not specifically limited, and these may be added at a time. The container to be used may be the same one as that to be used in the above-mentioned step 2a.

(Step 3b—Melting of Mixed Salt of Potassium Nitrate and Fusing Agent—)

In the step 3b, the mixed salt obtained in the step 2b is melted by heating. The melting is conducted at a temperature falling within a range of from the melting point (330° C.) of potassium nitrate to the boiling point (500° C.) thereof. In particular, it is more preferable that the melting temperature is from 350 to 470° C. from the viewpoint of the balance between the surface compressive stress (CS) to be given to a glass and the depth of the compressive stress layer (DOL) and of the strengthening time. The stirring time is preferably from 1 minute to 10 hours, more preferably from 10 minutes to 2 hours.

In a case where sediments form in the molten salt obtained through the above-mentioned step 2a and the step 3a, or through the step 2b and the step 3b, by adding a fusing agent thereto, the molten salt is kept statically until the sediments precipitate in the bottom of the container, before the chemical strengthening treatment for a glass. The sediments contain the fusing agent exceeding the saturation solubility thereof, and salts formed through exchange of cation in the fusing agent in the molten salt.

The molten salt for use in the production method of the present invention has an Na concentration of preferably 500 ppm by weight or more, more preferably 1,000 ppm by weight or more. The Na concentration of 500 ppm by weight or more in the molten salt is preferred since the low-density layer can easily deepen in the acid treatment step to be mentioned hereinunder. The upper limit of the Na concentration is not specifically defined, and is acceptable to a level at which a desired surface compressive stress (CS) can be obtained.

The molten salt used for chemical strengthening treatment once or more contains sodium released from a glass. Therefore, when the Na concentration is already within the above-mentioned range, glass-derived sodium may be used as such for the Na source, or when the Na concentration is insufficient or when a fresh molten salt that has not been used for chemical strengthening treatment is used, the Na concentration may be controlled by adding an inorganic sodium salt such as sodium nitrate.

As described above, a molten salt can be prepared according to the above-mentioned step 2a and the step 3a, or the step 2b and the step 3b.

(Chemical Strengthening)

Next, using the prepared molten salt, chemical strengthening treatment is performed. In the chemical strengthening treatment, a glass is immersed in a molten salt and the metal ion (Na ion) in the glass is substituted with a metal ion (K ion) having a larger ionic radius in the molten salt. Through the ion exchange, the composition of the glass surface is changed, and the glass surface is densified to form a compressive stress layer 20 [(a) to (b) in FIG. 2]. The densification of the glass surface generates compressive stress to strengthen the glass.

In fact, the density of chemically strengthened glass gradually increases from the outer edge of the interlayer 30 (bulk) existing in the center of the glass toward the surface of the compressive stress layer, and therefore between the interlayer 30 and the compressive stress layer 20, there exists no definite boundary at which the density suddenly changes. Here, the interlayer means a layer existing in the center part of the glass and surrounded by the compressive stress layer. The interlayer is a layer not undergone ion exchange, differing from the compressive stress layer.

Specifically, the chemical strengthening treatment in the present invention is performed by the following step 4.

Step 4: Chemical Strengthening Treatment for Glass

In the step 4, a glass is preheated, and the temperature of the molten salt prepared in the above-mentioned step 2a and the step 3a or the step 2b and the step 3b is adjusted to a temperature for chemical strengthening. Next, the preheated glass is immersed in the molten salt for a predetermined period of time, then the glass is drawn up from the molten salt and left cooled. Preferably, prior to the chemical strengthening treatment, the glass is processed for shaping in accordance with the use thereof, for example, through mechanical processing such as cutting, end fsurace machining, drilling, etc.

The glass preheating temperature depends on the temperature at which the glass is immersed in a molten salt, but, in general, preferably 100° C. or higher.

The chemical strengthening temperature is preferably not higher than the strain point of the glass to be strengthened (generally 500 to 600° C.), but for obtaining a greater compressive stress layer depth, particularly preferably 350° C. or higher.

The immersion time for the glass in a molten salt is preferably from 1 minute to 10 hours, more preferably from 5 minutes to 8 hours, even more preferably from 10 minutes to 4 hours. Falling within the range, it is possible to obtain a chemically strengthened glass excellent in the balance between the surface strength and the depth of the compressive stress layer.

In the production method of the present invention, the following steps are performed after the chemical strengthening treatment.

Step 5: Washing of the Glass

Step 6: Acid Treatment of the Glass after Step 5

At the time after the above-mentioned step 6, the glass surface further has a low-density layer 10 in which the surface layer of the compressive stress layer has been denatured, specifically, the density thereof has been reduced [(b) to (c) in FIG. 2]. The low-density layer is formed through leaching of Na and K from the outermost surface of the compressive stress layer, and in place of these, H has penetrated (substituted) therein.

The step 5 and the step 6 are described in detail hereinunder.

(Step 5—Washing of Glass—)

In the step 5, the glass is washed with industrial water, ion-exchanged water or the like. Above all, ion-exchanged water is preferred. The washing condition may vary depending on the washing liquid to be used, but in a case where ion-exchanged water is used, it is preferable that the glass is washed at 0 to 100° C. from the viewpoint of completely removing the adhered salts.

(Step 6—Acid Treatment—)

In the step 6, the glass washed in the step 5 is further subjected to an acid treatment.

In the acid treatment for a glass, a chemically strengthened glass is immersed in an acidic solution, whereby Na and/or K in the surface of the chemically strengthened glass can be substituted with H.

The solution is not specifically limited so far as it is acidic and has a pH of less than 7, in which the acid to be used may be a weak acid or a strong acid. Specifically, the acid is preferably hydrochloric acid, sulfuric acid, phosphoric acid, acetic acid, oxalic acid, carbonic acid, citric acid, etc. These acids may be used either singly or as combined.

The temperature for performing the acid treatment varies depending on the type and the concentration of the acid to be used and the treating time, but is preferably 100° C. or lower.

The time for performing the acid treatment also varies depending on the type, the concentration and the temperature of the acid to be used, but is preferably from 10 seconds to 5 hours from the viewpoint of productivity, more preferably from 1 minute to 2 hours.

The concentration of the solution for performing the acid treatment varies depending on the type and the temperature of the acid to be used and the treating time, but is preferably a concentration in which risk of container corrosion is less, and specifically, the concentration thereof is preferably from 0.1 wt % to 20 wt %.

The low-density layer is removed in alkali treatment to be mentioned below, and a thicker low-density layer is preferred as the glass surface is easy to remove. Accordingly, the thickness of the low-density layer is preferably 5 nm or more from the viewpoint of the amount of glass surface removal, more preferably 20 nm or more. The thickness of the low-density layer may be controlled by controlling the fusing agent concentration, the sodium concentration, the temperature, the time and the like in the chemical strengthening step.

The density of the low-density layer is preferably lower than the density in the region (bulk) deeper than the ion-exchanged compressive stress layer, from the viewpoint the glass surface removability.

The thickness of the low-density layer may be determined from the period (Δθ) measured in X-ray reflectometry (XRR).

The density of the low-density layer may be determined from the critical angle (θc) measured in XRR.

In a simplified manner, formation of a low-density layer and the thickness of the layer may be confirmed through observation of the cross section of a glass with a scanning electronic microscope (SEM).

In the production method of the present invention, the following step is performed after the acid treatment.

Step 7: Alkali Treatment

In the step 7, a part or all of the low-density layer formed up to the step 6 may be removed [(c) to (d) in FIG. 2].

The step 7 is described in detail hereinunder.

(Step 7—Alkali Treatment—)

In the step 7, the glass having been subjected to the acid treatment in the step 6 is further subjected to an alkali treatment.

In the alkali treatment, the chemically strengthened glass is immersed in a basic solution, whereby a part or all of the low-density layer is removed.

The solution is not specifically limited so far as it is basic and has a pH of more than 7, in which any of a weak base or a strong base is usable. Specifically, a base such as sodium hydroxide, potassium hydroxide, potassium carbonate, sodium carbonate or the like is preferred. These bases may be used either singly or as combined.

The temperature for performing the alkali treatment varies depending on the type and the concentration of the base to be used and the treating time, but is preferably from 0 to 100° C., more preferably from 10 to 80° C., even more preferably from 20 to 60° C. The temperature range is preferred as causing no risk of glass corrosion.

The time for performing the alkali treatment also varies depending on the type, the concentration and the temperature of the base to be used, but is preferably from 10 seconds to 5 hours from the viewpoint of productivity, more preferably from 1 minute to 2 hours.

The concentration of the solution for performing the alkali treatment varies depending on the type and the temperature of the base to be used and the treating time, but is preferably from 0.1 wt % to 20 wt % from the viewpoint of glass surface removability.

Through the above-mentioned alkali treatment, a part or all of the low-density layer with H having penetrated thereinto is removed and the surface layer in which the hydrogen concentration profile satisfies the specific relational equation (I) described above is exposed out. Accordingly, a chemically strengthened glass having an improved surface strength can be obtained. Further, since the low-density layer is removed, the flaws existing in the glass surface are also removed at the same time. Therefore, it is considered that this point also contributes to the strength improvement.

In addition, in the production method of the present invention, by polishing the glass surface before the chemical strengthening treatment, large surface flaws are removed in advance. It may be conjectured that according to this pre-polishing, the chemical strengthening treatment, and the acid and alkali treatments, macro flaws and micro flaws on the glass surface are removed, whereby the surface strength of the glass is remarkably improved.

Between the above-mentioned acid treatment step 6 and the alkali treatment step 7, or after the alkali treatment step 7, it is preferable to perform a washing step like the step 5.

In the production method of the present invention, the chemical liquids to be handled are highly safe and therefore the method does not require any special equipment. Accordingly, a chemically strengthened glass whose surface strength has dramatically increased can be obtained safely and efficiently.

The amount of the low-density layer to be removed depends on the alkali treatment condition. An embodiment in which the low-density layer 10 has been completely removed is shown in (d) of FIG. 2, however, a part of the low-density layer 10 may be removed while a part thereof has remained. From the viewpoint of strength improvement, the effect can be obtained even when not all the low-density layer is removed, but from the viewpoint of stably securing the transmittance of glass, it is preferable that all the low-density layer is removed.

According to the method for producing a chemically strengthened glass of the present invention, even when polished, a chemically strengthened glass with an improved surface strength can be obtained. Then, since the treatment can be allowed to proceed by immersing in the solution, the production method is efficient from the standpoints that it is liable to cope with various glass shapes and large-area glasses; and that the both surfaces of the glass can be simultaneously treated. In addition, even in the case where latent flaws are present in advance on the glass surface, a chemically strengthened glass free from an appearance failure due to a pit and with an improved surface strength can be obtained. Furthermore, as compared with etching treatment using hydrofluoric acid or the like, the treatment in the present invention is highly safe and inexpensive.

EXAMPLES

The present invention is described specifically with reference to Examples given below, but the present invention is not limited thereto.

<Evaluation Method>

Various evaluations in present Examples were performed according to the analysis methods mentioned below.

(Evaluation of Glass: Surface Stress)

The compressive stress value of the compressive stress layer and the depth of the compressive stress layer in the chemically strengthened glass of the present invention can be measured using EPMA (electron probe microanalyzer) or a surface stress meter (for example, FSM-6000 manufactured by Orihara Manufacturing Co., Ltd.), etc. In Examples, the surface compressive stress value (CS, unit: MPa) and the depth of the compressive stress layer (DOL, unit: μm) were measured using a surface stress meter (FSM-6000) manufactured by Orihara Manufacturing Co., Ltd.

(Evaluation of Glass: Removal Amount)

The removal amount thickness of a glass was determined by measuring the weight thereof before and after chemical liquid treatment, using an analytical electronic balance (HR-202i, manufactured by A&D Company, Limited), and converting the found value into a thickness according to the following equation. (Removal amount thickness per one surface)=((weight before treatment)−(weight after treatment))/(glass specific gravity)/treated area/2 At this time, the calculation was made while defining the glass specific gravity as 2.41 (g/cm³). (Evaluation of Glass: Texture Direction Index (Stdi))

First of all, a shape image was obtained by using an atomic force microscope (XE-HDM, manufactured by Park Systems Corporation) under conditions of measurement mode: non-contact mode, scanning size: 10 μm×5 μm, color scale: ±1 nm, scanning speed: 1 Hz, cantilever: Non-contact Cantilever (Item: PPP-NCHR 10M, manufactured by Park Systems Corporation). Thereafter, a leveling treatment and an L-filtering treatment (ISO value: 2.0 μm) of the shape image were performed by using an image analysis software (SPIP 6.2.6, manufactured by Image Metrology Inc.), and a texture direction index (Stdi) was determined by a roughness analysis.

(Evaluation of Glass: Texture Aspect Ratio (Str20))

First of all, a shape image was obtained by using an atomic force microscope (XE-HDM, manufactured by Park Systems Corporation) under conditions of measurement mode: non-contact mode, scanning size: 10 μm×5 μm, color scale: ±1 nm, scanning speed: 1 Hz, cantilever: Non-contact Cantilever (Item: PPP-NCHR 10M, manufactured by Park Systems Corporation). Thereafter, a leveling treatment and an L-filtering treatment (ISO value: 2.0 μm) of the shape image were performed by using an image analysis software (SPIP 6.2.6, manufactured by Image Metrology Inc.), and a texture aspect index (Str20) was determined by a roughness analysis.

(Evaluation of Glass: Surface Strength)

The glass surface strength was measured according to the ball-on-ring (BOR) test. FIG. 1 shows a schematic view for explaining the ball-on-ring test employed in the present invention. A glass sheet 1 was, while kept set horizontally, pressurized by a pressurizing jig 2 made of SUS304 (hardened steel, diameter 10 mm, mirror-finished) to measure the surface strength of the glass sheet 1.

In FIG. 1, the glass sheet 1 to be a sample is horizontally disposed on a receiving jig 3 made of SUS304 (diameter: 30 mm, curvature radius of the contact part R: 2.5 mm, the contact part is hardened steel, mirror-finished). Above the glass sheet 1, a pressurizing jig 2 for pressurizing the glass sheet 1 is arranged.

In this embodiment, the center region of the glass sheet 1 obtained in Examples and Comparative Examples was pressurized from the above of the glass sheet 1. The test condition is as mentioned below.

Descending Rate of Pressurizing Jig 2: 1.0 (mm/min)

In this test, the fracture load (unit: N) at which the glass was fractured was taken as a BOR surface strength. The average value of twenty measured values thereof was taken as a surface strength F. However, in a case where the fracture origin of the glass sheet was separated from a loading point of the ball by 2 mm or more, the obtained value was excluded from the data for calculating the average value.

(Evaluation of Glass: Hydrogen Concentration)

According to the method described in the section of [Method for Measuring Hydrogen Concentration Profile] given hereinabove, the hydrogen concentration profile was determined and the relational equation (I) was derived therefrom.

Example 1 Polishing Step

An aluminosilicate glass having dimensions of 50 mm×50 mm×0.70 mm was prepared, cerium oxide having an average particle diameter of 1.2 μm was dispersed in water to prepare a slurry having a specific gravity of 0.9, and the both surfaces of the aluminosilicate glass were simultaneously polished in a depth of 3.0 μm per surface with a polishing pad (nonwoven type) under conditions of a polishing pressure of 10 kPa. A surface roughness (Ra) as measured by the AFM measurement was 0.45 nm.

AFM measurement conditions: Atomic force microscope (XE-HDM, manufactured by Park Systems Corporation), scanning size: 10 μm×5 μm, color scale: ±1 nm, scanning speed: 1 Hz

(Chemical Strengthening Step)

In an SUS-made cup, 9,700 g of potassium nitrate, 890 g of potassium carbonate, and 400 g of sodium nitrate were introduced, and the contents were heated to 450° C. by a mantle heater to prepare a molten salt containing 6 mol % of potassium carbonate and 10,000 ppm by weight of sodium. The glass obtained in the polishing step was preheated to 200 to 400° C. and then subjected to a chemical strengthening treatment by immersing in the molten salt at 450° C. for 2 hours for ion exchange and cooling to around room temperature. The resultant chemically strengthened glass was washed with water and subjected to the next step.

Composition (in terms of mol %) of the aluminosilicate glass (specific gravity: 2.41): SiO₂ 68%, Al₂O₃ 10%, Na₂O 14%, MgO 8%

(Acid Treatment Step)

In a resin-made tank, 6.0 wt % of nitric acid (HNO₃, manufactured by Kanto Chemical Co., Inc.) was prepared and subjected to temperature adjustment to 41° C. by using a fluorine resin-covered heater (KKS14A, manufactured by Hakko Electric Co., Ltd.). The glass obtained in the above-described chemical strengthening step was immersed in the nitric acid whose temperature was adjusted, for 120 seconds to perform the acid treatment, followed by washing with pure water several times. The resultant glass was subjected to the next step.

(Alkali Treatment Step)

An aqueous solution of 4.0 wt % sodium hydroxide was prepared in a resin-made tank and subjected to temperature adjustment to 40° C. by using a fluorine resin-covered heater (KKS14A, manufactured by Hakko Electric Co., Ltd.). The glass obtained in the acid treatment step was immersed in the sodium hydroxide aqueous solution whose temperature was adjusted, for 120 seconds to perform the alkali treatment, followed by washing with pure water several times and then drying with air blowing.

Thus, a chemically strengthened glass of Example 1 was obtained.

Example 2

A chemically strengthened glass was produced in the same manner as in Example 1, except that in the polishing step, cerium oxide having an average particle diameter of 0.9 μm was used as the polishing agent; and that the polishing pad was changed to a polishing pad of a suede type.

Example 3

A chemically strengthened glass was produced in the same manner as in Example 2, except that in the polishing step, the polishing pad was changed to a polishing pad of a hard urethane type; and that in the chemical strengthening step, the sodium amount in the molten salt, the chemical strengthening treatment temperature, and the chemical strengthening treatment time were changed to values shown in Table 1, respectively.

Comparative Example 1

A chemically strengthened glass was produced in the same manner as in Example 1, except that in the chemical strengthening step, the sodium amount in the molten salt was changed to a value shown in Table 1, and the addition amount of potassium carbonate was changed to 0 g; and that the acid treatment step and the alkali treatment step were omitted.

Comparative Example 2

A chemically strengthened glass was produced in the same manner as in Example 2, except that in the polishing step, cerium oxide having an average particle diameter of 0.7 μm was used as the polishing agent; that in the chemical strengthening step, the sodium amount in the molten salt was change to a value shown in Table 1, and the addition amount of potassium carbonate was changed to 0 g; and that the acid treatment step and the alkali treatment step were omitted.

Comparative Example 3

A chemically strengthened glass was produced in the same manner as in Example 2, except that in the chemical strengthening step, the sodium amount in the molten salt was change to a value shown in Table 1, and the addition amount of potassium carbonate was changed to 0 g; and that the acid treatment step and the alkali treatment step were omitted.

Reference Example 1

A chemically strengthened glass was produced in the same manner as in Example 2, except that in the polishing step, cerium oxide having an average particle diameter of 0.7 μm was used as the polishing agent.

Reference Example 2

A chemically strengthened glass was produced in the same manner as in Example 2, except that in the polishing step, cerium oxide having an average particle diameter of 0.7 μm was used as the polishing agent; and in the chemical strengthening step, the sodium amount in the molten salt, the chemical strengthening treatment temperature, and the chemical strengthening treatment time were changed to values shown in Table 1, respectively.

The thus-obtained chemically strengthened glass was evaluated for various properties. The results are shown in Table 1.

FIGS. 3 to 5 show graphs in which the hydrogen concentration profile in the surface layer of the respective chemically strengthened glasses obtained in the respective Examples and Comparative Examples was plotted.

Furthermore, FIGS. 6 to 13 show images observed by AFM with respect to glass surfaces before and after the acid treatment and the alkali treatment of the respective chemically strengthened glasses obtained in the respective Examples, Comparative Examples, and Reference Examples.

Further, FIG. 14 shows a Weibull plot of BOR surface strength evaluation of each of chemically strengthened glasses obtained in Example 1 and Comparative Example 1. FIG. 14 shows a Weibull plot of BOR surface strength evaluation of an aluminosilicate glass sheet sample having a thickness of 0.70 mm. The horizontal axis of the graph indicates a logarithm ln (σ) of the fracture load σ (N), and the vertical axis thereof indicates a cumulative fracture probability percentage P (%) relative to the sample in each of the two groups.

TABLE 1 Comparative Comparative Comparative Reference Reference Example 1 Example 2 Example 3 Example 1 Example 2 Example 3 Example 1 Example 2 Type of Glass alumino- alumino- alumino- alumino- alumino- alumino- alumino- alumino- silicate silicate silicate silicate silicate silicate silicate silicate glass glass glass glass glass glass glass glass Polishing before chemical strengthening Performed Performed Performed Performed Performed Performed Performed Performed Polishing flaws Present Present Present Present Present Present Absent Absent Chemical K₂CO₃ mol % 6 6 6 0 0 0 6 6 strengthening Na amount wt ppm 10,000 10,000 6,000 2,000 2,000 2,000 10,000 6,000 Temperature ° C. 450 450 430 450 450 450 450 430 Time min 120 120 360 120 120 120 120 360 Acid treatment Chemical liquid type HNO₃ HNO₃ HNO₃ — — — HNO₃ HNO₃ Concentration wt % 6 6 6 — — — 6 6 Temperature ° C. 40 40 40 — — — 40 40 Time sec 120 120 120 — — — 120 120 Alkali treatment Chemical liquid type NaOH NaOH NaOH — — — NaOH NaOH Concentration wt % 4 4 4 — — — 4 4 Temperature ° C. 40 40 40 — — — 40 40 Time sec 120 120 120 — — — 120 120 Sheet thickness (t) mm 0.70 0.70 0.51 0.70 0.70 0.70 0.70 0.51 Surface Strength (F) N 1303 1305 563 564 483 485 1291 798 F/t² N/mm² 2658 2664 2196 1151 985 989 2635 3020 Surface removal amount nm 189 207 212 — — — 198 210 Texture direction index (Stdi) 0.51 0.84 0.30 0.24 0.40 0.46 0.88 0.80 Texture aspect ratio (Str20) 0.37 0.66 0.04 0.05 0.50 0.33 0.50 1.00 Equation (I) a −0.136 −0.138 −0.235 −0.305 −0.379 −0.355 −0.195 −0.253 b 0.059 0.093 0.125 0.148 0.184 0.187 0.093 0.131 CS MPa 877 871 922 949 939 932 870 928 DOL μm 28 28 40 27 27 28 28 40

From the results in Table 1, Examples 1 to 3 each having a texture direction index (Stdi) of 0.30 or more and satisfying the relational equation (I) were significantly improved in the surface strength as compared to Comparative Examples 1 to 3. In addition, Examples 1 and 2 each having a texture aspect ratio (Str20) of 0.10 or more were more improved in the surface strength than Example 3.

In addition, from the results of FIG. 14, the average fracture load was 1,303 N in Example 1, whereas it was 564 N in Comparative Example 1. The 10% fracture load (B10) was 1,128 N in Example 1, whereas it was 488 N in Comparative Example 1; and the 1% fracture load (B1) was 927 N in Example 1, whereas it was 402 N in Comparative Example 1. It can be seen from these results that Example 1 does not produce low-strength products, and the products obtained have greatly improved reliability for the surface strength.

While the invention has been described in detail and with reference to specific embodiments thereof, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope thereof. The present application is based on a Japanese patent application filed on Jul. 19, 2013 (Japanese Patent Application No. 2013-151116), and the content thereof is herein incorporated by reference.

INDUSTRIAL APPLICABILITY

According to the present invention, a chemically strengthened glass whose surface strength has been dramatically improved can be obtained safely and inexpensively. The chemically strengthened glass of the present invention is usable as a cover glass for displays such as mobile phones, digital cameras, and touch panel displays.

DESCRIPTION OF REFERENCE NUMERALS AND SIGNS

-   -   10: Low-density layer     -   20: Compressive stress layer     -   30: Interlayer 

The invention claimed is:
 1. A glass sheet, having a compressive stress layer formed in a surface layer thereof according to an ion exchange method, wherein a surface of the glass sheet has polishing flaws, the glass sheet has a texture direction index (Stdi) of 0.30 or more, a surface strength F (N) of the glass sheet measured by a ball-on-ring test is at least a value of (1400×t²), wherein t (mm) is a thickness of the glass sheet, and a hydrogen concentration Y in a region to a depth X from a surface of the glass sheet satisfies relational equation (I) at X=from 0.1 to 0.4 (μm): Y=aX+b  (I) wherein: Y is the hydrogen concentration measured as H₂O, (mol/L); X is the depth from the surface of the glass sheet (μm); a is −0.300 or more; and b is 0.220 or less, wherein the ball-on-ring test is conducted by: placing the glass sheet on a stainless ring whose diameter is 30 mm and whose contact part has a roundness with a curvature radius of 2.5 mm; applying a load on a center of the ring by the ball under a static loading condition, while a steel ball having a diameter of 10 mm is kept in contact with the glass sheet; and measuring a BOR surface strength which is a fracture load (unit: N) at which the glass sheet is fractured and determining an average value of twenty measured values of the BOR surface strength as the surface strength F, provided that in a case where a fracture origin of the glass sheet is apart from a loading point of the ball by 2 mm or more, the obtained value is excluded from data for calculating the average value.
 2. The glass sheet according to claim 1, wherein the glass sheet is made of an aluminosilicate glass, an aluminoborosilicate glass or a soda-lime glass.
 3. The glass sheet according to claim 1, wherein the glass sheet has a texture aspect ratio (Str20) of 0.10 or more.
 4. The glass sheet according to claim 1, wherein a thickness of the glass sheet is 5 mm or less.
 5. A method for producing the glass sheet as defined in claim 1, the method comprising: polishing a surface of a glass sheet comprising sodium; bringing the glass sheet into contact with an inorganic salt comprising potassium nitrate, thereby performing ion exchange of a Na ion in the glass sheet with a K ion in the inorganic salt, after the polishing; washing the glass sheet after the ion exchange; subjecting the glass sheet to an acid treatment after the washing; and subjecting the glass sheet to an alkali treatment after the acid treatment, wherein the inorganic salt further comprises at least one salt selected from the group consisting of K₂CO₃, Na₂CO₃, KHCO₃, NaHCO₃, K₃PO₄, Na₃PO₄, K₂SO₄, Na₂SO₄, KOH and NaOH.
 6. The method according to claim 5, wherein the inorganic salt has an Na concentration of 500 ppm by weight or more.
 7. The method according to claim 5, wherein the inorganic salt contains K₂CO₃ in an amount of 0.1 mol % or more.
 8. The method according to claim 5, further comprising washing the glass sheet after the acid treatment.
 9. The method according to claim 5, further comprising washing the glass sheet after the alkali treatment.
 10. The method according to claim 5, wherein a solution having a pH of less than 7 is used in the acid treatment.
 11. The method according to claim 10, wherein the solution having the pH of less than 7 is a weak acid.
 12. The method according to claim 10, wherein the solution having the pH of less than 7 is a strong acid.
 13. The method according to claim 5, wherein the acid treatment is performed at a temperature of 100° C. or lower.
 14. The method according to claim 5, wherein a time for performing the acid treatment is from 10 seconds to 5 hours.
 15. The method according to claim 10, wherein the solution having the pH of less than 7 has an acid concentration of from 0.1 wt % to 20 wt %.
 16. The method according to claim 5, wherein a solution having a pH of more than 7 is used in the alkali treatment.
 17. The method according to claim 16, wherein the solution having the pH of more than 7 is a weak base.
 18. The method according to claim 16, wherein the solution having the pH of more than 7 is a strong base.
 19. The method according to claim 5, wherein the alkali treatment is performed at a temperature of from 0 to 100° C.
 20. The method according to claim 5, wherein a time for performing the alkali treatment is from 10 seconds to 5 hours.
 21. The method according to claim 16, wherein the solution having the pH of more than 7 has an alkali concentration of from 0.1 wt % to 20 wt %. 